US4314594A - Reducing magnetic hysteresis losses in cores of thin tapes of soft magnetic amorphous metal alloys - Google Patents

Reducing magnetic hysteresis losses in cores of thin tapes of soft magnetic amorphous metal alloys Download PDF

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US4314594A
US4314594A US06/144,895 US14489580A US4314594A US 4314594 A US4314594 A US 4314594A US 14489580 A US14489580 A US 14489580A US 4314594 A US4314594 A US 4314594A
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core
magnetic
tape
cooling
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Friedrich Pfeifer
Wernfried Behnke
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Vacuumschmelze GmbH and Co KG
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F13/00—Apparatus or processes for magnetising or demagnetising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15341—Preparation processes therefor
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S428/00—Stock material or miscellaneous articles
    • Y10S428/922—Static electricity metal bleed-off metallic stock
    • Y10S428/9265—Special properties
    • Y10S428/928—Magnetic property
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12431—Foil or filament smaller than 6 mils
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12535—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.] with additional, spatially distinct nonmetal component
    • Y10T428/12583—Component contains compound of adjacent metal
    • Y10T428/1259—Oxide

Definitions

  • the field of this invention lies in techniques for reducing magnetic hysteresis losses in thin magnetic tapes.
  • amorphous metal alloys can be produced from a melt of corresponding composition by cooling the melt so rapidly that it solidifies without crystallization.
  • such alloys can be directly formed in the shape of a thin tape or ribbon, whose thickness, for example, can range up to several hundredths of a millimeter and whose width, for example, can range up several millimeters (compare, for example German Offenlegungschrift No. 25 00 846 and German Offenlegungsschrift No. 26 06 581).
  • Amorphous alloys can be distinguished from crystal alloys be means of X-ray diffraction measurements.
  • the intensity of X-ray diffraction bands exhibited by amorphous metal alloys is found to alter with the diffraction angle, only slowly as is comparable to the characteristic X-ray diffraction patterns observed in liquids or common glass.
  • an amorphous metal alloy can be totally amorphous, or it can be comprised of a two-phase mixture of the amorphous and the crystalline states.
  • the term "amorphous metal alloys", or equivalent as used herein generally has reference to an alloy which is at least 50%, and preferably at least 80%, amorphous on a 100 total weight percent alloy basis.
  • Each amorphous metal alloy has a characteristic temperature, the so-called “crystallization temperature", such that, if the amorphous alloy is heated to, or above, this temperature, said alloy passes into its crystalline state. However, the amorphous condition is retained during thermal treatments below such crystallization temperature.
  • M represents at least one of the metals iron, cobalt and nickel
  • X represents at least one of the so-called glass-forming elements boron, carbon, silicon and/or phorphorus
  • y is a numerical value which lies between 0.60 and 0.95.
  • such amorphous alloys can also contain additional metals, particularly, titanium, zirconium, vanadium, niobium, tantalum, chromium, molybdenum, tungsten, manganese, palladium, platinum, copper, silver and/or gold.
  • such an amorphous alloy can contain the elements aluminum, gallium, indium, germanium, tin, arsenic, antimony, bismuth and/or beryllium (compare German Offenlegungsschrift No. 25 46 676, German Offenlegungsschrift No. 25 53 003, German Offenlegungsschrift No. 26 05 615 and German Offenlegungsschrift No. 26 28 362).
  • Soft-magnetic amorphous alloys with their respective associated magnetic properties are of great interest for technical utilization since they, as previously mentioned, can be directly produced in the shape of thin tapes.
  • crystalline soft-magnetic metal alloys now common in the art a plurality of milling steps with numerous intermediate annealings are required in order to produce correspondingly thin tapes.
  • soft magnetic as used herein reference is had to such an alloy which is relatively easily magnetized or demagnetized.
  • the remanence and the remanence ratio as is common is crystalline soft-magnetic materials, was increased in relation to non-annealed cores.
  • the remanence and the remanence ratio in relation to non-annealed cores was decreased by means of annealing and subsequent cooling in a transverse magnetic field, so that the corresponding inductance-field intensity curves have a flatter (smoother) gradient than those of the unannealed cores, and exhibit a so-called F-characteristic due to their flat (shallow gradient) course.
  • the magnetic hysteresis losses in these known experiments could only be decreased to values which are approximately double the magnetic hysteresis losses in tapes consisting of comparable soft magnetic alloys.
  • loss values of 18 mW/cm 3 equal to 2.4 W/kg were obtained, whereas the corresponding losses in tapes consisting of low-loss conventional crystalline soft-magnetic alloys only amount to approximately 1 W/kg. Only in the one case mentioned was a loss value of approximately 1.33 W/kg obtained in alternating cited magnetic field.
  • the core involved has been cooled with a high cooling speed which is virtually no longer capable of being technically controlled, and, moreover, it exhibited a remanence ratio of 0.2 which no longer results in a flat (shallow) F-loop.
  • precisely a hysteresis curve in the form of an F-loop is desirable in simultaneous conjunction with magnetic hysteresis losses which are as low as possible.
  • this invention relates to a method for reducing magnetic hysteresis losses in a magnetic core formed of thin tape comprised of a soft magnetic amorphous metal alloy, whereby such a tape in the form of a magnetic core wound therefrom is first heated to a temperature above its Curie temperature, but below its crystallization temperature, for the purpose of mechanical relaxation, or tension release, and afterwards is then allowed to cool in a controlled manner to a temperature below such Curie temperature. Both the heating and the cooling are carried out in an oxidizing atmosphere.
  • the invention has as a primary object the further decreasing (or reducing) of magnetic hysteresis losses in soft-magnetic amorphous metal alloys beyond that heretofore realized.
  • Another object is to achieve such a goal by using a method of the general type above related, and simultaneously to obtain an F-characteristic in the hysteresis curve which is as flat as possible.
  • a surprising and unexpected feature of this invention is that such objects are achieved by conducting an annealing and a subsequent cooling of a core of thin metal alloy tape in air or other oxydizing atmosphere.
  • the thermal treatment sequence of annealing and controlled cooling in air leads surprisingly and unexpectedly to low magnetic hysteresis losses, and also surprisingly to low remanences and remanence ratios.
  • a stressing or tensioning of such a thin tape consisting of an amorphous soft magnetic alloy by means of a thin oxide layer deposited, or existing, on the tape's surface plays a role.
  • a corresponding effect may also be obtained with other oxidizing media.
  • FIGURE a plot showing the relation between effective magnetic field intensity as abscissae versus maximum induction amplitude as ordinates for each of three cores, all similarly formed with the same soft magnetic amorphous metal alloy thin tape, all processed under the teachings of this invention, but each being subjected to different processing conditions.
  • oxidizing atmosphere conventional reference is had to a gaseous atmosphere in which an oxidation reaction can occur.
  • such an atmosphere should comprise at least about 10% by weight of oxygen (O 2 ) with the balance up to 100 weight percent thereof being an inert gas.
  • Suitable inert gases include, for examples, nitrogen, neon, argon, or other Group VIII gas (of the Periodic Table of the Elements), or the like.
  • a particularly preferred oxidizing atmosphere comprises air.
  • Another suitable oxidizing atmosphere is comprised of from about 25 to 80 weight percent oxygen with the balance up to 100 weight percent thereof on a total atmosphere weight basis being an inert gas.
  • Another suitable oxidizing atmosphere comprises only oxygen.
  • the pressure at which the oxidizing atmosphere is maintained during practice of the process of the present invention can vary widely. Atmospheric pressures are particularly convenient, but super atmospheric and sub-atmospheric pressures can be employed. For example, one suitable pressure range extends from about 5 ⁇ 10 4 to 2 ⁇ 10 5 N/m 2 .
  • the cooling rate utilized in the practice of the present invention can vary substantially, but is typically in the range from about 20° to 300° C. per hour. As hereinbelow indicated, particular values in this range may be more suitable for tapes composed of certain alloys, as opposed to other tapes of different alloys.
  • the starting tapes used in this invention are amorphous and soft magnetic, as indicated above. Commonly, such a tape has a thickness ranging from about 0.01 to 0.1 millimeters (0.03 to 0.06 mm being preferred), and has a width ranging from about 1 to 30 millimeters (1 to 20 mm being preferred).
  • Such starting tapes are known to the prior art, as are the methods for their manufacture.
  • the composition of the metal alloy forming the tape can vary widely, as those skilled in the art will appreciate.
  • a starting tape is incorporated into a core before being processed according to this invention.
  • magnetic core or simply, “core”
  • core reference is had to a conventional configuration comprised of magnetic material and incorporating a plurality of spirally or similarly wound layers of a thin tape of soft-magnetic amorphous metal alloy, as above characterized.
  • Such an individual core configuration can have, for example, a small doughnut-like shape which is adapted for placing in a spatial relationship to current-carrying conductors, as those skilled in the art will readily appreciate.
  • Preferably such an individual core configuration is shaped and adapted for use as a transformer core, particularly for a transformer core in a so-called medium frequency power supply. Methods for making cores are well known to the prior art.
  • a tape is preferably exposed to, or maintained in, during the cooling step, a magnetic field at least sufficient to magnetize such tape nearly to its saturation point.
  • saturation point or equivalent, reference is had to the condition in which, after a magnetic field strength becomes sufficiently large, further increase in the magnetic field strength produces no additional magnetization in a magnetic material.
  • the field is preferably applied either longitudinally or transversely relative to a given tape (preferably longitudinally).
  • w ranges from about 20 to 80 atomic percent
  • x ranges from about 0 to 60 atomic percent
  • y ranges from about 0 to 20 atomic percent
  • z ranges from about 0 to 20 atomic percent
  • y+z ranges from 15 to 30 atomic percent, and in any given such metal alloy, the sum total of w, x, y, and z is 100 atomic percent.
  • a particularly preferred member is an alloy of the formula
  • a tape of such class following the teachings of this invention, is formed into a core and then heated to a temperature ranging from about 280° to 350° C. for a time of at least about 0.5 to 2 hours. Also, following such teachings, such a so heated shaped tape is cooled preferably to a temperature below about 200° C. at a cooling rate of from about 100° to 250° per hour. The heating and the cooling take place in an oxidizing atmosphere.
  • a magnetic core formed of a soft magnetic, amorphous tape which consists, for example, of the particular composition Fe 0 .40 Ni 0 .40 P 0 .14 B 0 .06 for at least approximately 0.5 through 2 hours at a temperature of between approximately 280° and 350° C., and then to cool it down to a temperature of 200° C. or less in a controlled manner, such as above indicated.
  • temperatures of between about 280° and 350° C. and while employing the cited minimum annealing times of approximately 0.5 through 2 hours, a complete mechanical tension release of the tapes can be obtained.
  • the longer minimum annealing times are to be used for the lower temperatures, and, conversely, the shorter times for the higher temperatures.
  • the temperatures lie above the Curie temperature of this type of alloy which temperature is approximately 230° C., and below the crystallization temperature of the alloy which temperature is about 360° C.
  • a cooling speed of approximately 100 to 250° C. per hour has been proven to be particularly advantageous for the controlled cooling in view of the magnetic parametrics desired.
  • the cooling-off in a longitudinal field is particularly advantageous if the smallest possible loss values are to be obtained.
  • magnetizing a tape of a core during the cooling-off process nearly to its saturation point in a transverse magnetic field, one can obtain magnetic characteristic values for a core which lie between the values obtained during cooling in the longitudinal field and the values obtained during cooling in the absence of a magnetic field.
  • magnetic hysteresis losses are somewhat higher than in the other types of magnetization.
  • magnetization nearly to the saturation point must proceed during the controlled cooling-off process from a temperature above the Curie temperature to a temperature below the Curie temperature.
  • magnetization nearly to the saturation point has reference to a magnetization of more than 60% of the saturation point. It is advantageous to come as close as possible to saturation, as those skilled in the art will appreciate.
  • the tape cores processed in accordance with the method of this invention are particularly well suited for transformer cores in so-called medium frequency power supplies, for example, a frequency of 20 kHz.
  • medium frequency power supplies for example, a frequency of 20 kHz.
  • a flat F-characteristic of the hysteresis curve of the transformer cores is an essential factor in a number of circuit applications for such power supplies.
  • Medium frequency power supplies in relation to power supplies with a frequency of, for example, 50 Hz, possess the advantage that the respective transformers can be constructed considerably smaller, and, in addition, the often interfering humming at 50 Hz is eliminated.
  • medium frequency power supplies are often employed, for example, in data processing equipment, office computers, cash registers and teletypewriters.
  • inventively treated tape cores consisting of amorphous soft-magentic alloy tapes are also suitable for utilization in the case of unipolar drives where a flat slope of the hysteresis curve is also of importance.
  • ring tape cores of 20 mm exterior and 10 mm interior diameter were produced from an approximately 2 mm wide and 0.05 mm thick tape consisting of a soft-magnetic amorphous alloy of the composition Fe 0 .40 Ni 0 .40 P 0 .14 B 0 .06.
  • the individual tape windings were insulated from one another by means of magnesium oxide powder.
  • the wound cores, each respectively consisting of 70 to 80 windings, were inserted into suitable protective aluminum troughs.
  • the cores in the protective troughs were then subjected to a 30 minute relaxation annealing at a temperature of approximately 325° C., which lies between the Curie temperature of the alloy of approximately 230° C. and the alloy crystallization temperature of approximately 360° C.
  • the cores were allowed to cool off in a controlled manner at a cooling rate of approximately 200° C. per hour to a temperature below the Curie temperature; in the present case, to a temperature of approximately 100° C. Additional cooling to ambient temperatures proceeded in an uncontrolled manner.
  • the annealing and subsequent controlled cooling-off proceeded in air under different conditions.
  • a group of the cores was annealed and cooled in a magnetic field running in peripheral direction of the individual core; i.e., in a magnetic field running parallel to the longitudinal direction of the wound tape, in a so-called longitudinal field, which was produced by means of a winding secured to the core and which magnetized the amorphous alloy near to its saturation value with a field intensity of 16 A/cm.
  • Another group of the cores was annealed and cooled in a magnetic field directed vertically to the longitudinal direction of the tape, parallel to the winding axis of the core, a so-called transverse field.
  • the cores were brought into the field of a 10 cm-long rod magnet consisting of AlNiCo 26/6 having a cross sectional area of 4 by 4 cm 2 .
  • An additional group of the cores was annealed and cooled in the absence of a magnetic field.
  • induction-field intensity curves at 50 Hz were then measured with a vector measuring device. From these curves, the relative alternating field permeabilities ⁇ 4 , i.e., the permeability at a magnetic field intensity of 4 mA/cm, and ⁇ max , i.e., the maximum permeability, was determined. Moreover, the coercive force H c and the remanence B r were statically determined.
  • the ratio of the remanence B r to the saturation induction B s was determined, the so-called remanence ratio B r /B s , which is a good measure of the slope of the hysteresis curve and thus of the F-characteristic of of the hysteresis loop.
  • the magnetic hysteresis losses P Fe in an alternating magnetic field having maximum induction of 0.1 T and a frequency of 10 kHz and in an alternating magnetic field having a maximum induction of 0.2 T and a frequency of 20 kHz were measured.
  • test results were compiled in the following Table I together with the values measured on an unannealed ring tape core consisting of the same amorphous soft magnetic alloy.
  • the induction-field intensity curves measured at 50 Hz using the ring tape cores annealed and cooled in air are illustrated in the FIGURE.
  • the effective magnetic field intensity H eff is plotted in A/cm on the abscissa in a logarithmic scale, and the respective maximum amplitude B of the induction is also plotted in T in a logarithmic scale on the ordinate.
  • the curve a was measured on a core annealed and cooled in a longitudinal field; curve b was measured on a core annealed and cooled in the absence of a magnetic field; and the curve c was measured on a core annealed and cooled in a transverse field.
  • the curves illustrate an approximately linear increase in the induction with the field intensity. They have a very flat (or shallow) slope and thus show a marked or pronounced F-characteristic.
  • the remanence and the remanence ratio of the cores annealed and cooled in air is extremely small in relation to the non-annealed core, and to the cores annealed and cooled under hydrogen.
  • the decrease of both values is particularly remarkable in the core subjected to the annealing treatment (process) in the longitudinal field under air in relation to the values of the unannealed core.
  • the remanence and remanence ratio is normally increased by annealing with controlled cooling in the longitudinal field, as occurs, for example, in the case of the core which is annealed and cooled in the longitudinal field under hydrogen.
  • the Table I furthermore illustrates that the magnetic (or hysteresis) losses caused by annealing and subsequent controlled cooling in air are reduced as compared with those of the unannealed core to an extent far exceeding the reduction obtained with an annealing treatment under hydrogen.
  • the losses are particularly low in cores which are annealed and cooled without magnetic field and in the longitudinal field.
  • cores of tapes with a thickness of 0.05 mm consisting of conventional crystalline permalloys (approximately 76.5 percent by weight nickel, 4.5 percent by weight copper, 3 through 3.5 percent by weight molybdenum, and the balance up to 100 weight percent being iron)
  • values in magnetic hysteresis losses of 10 through 12 W/kg are obtained at 0.2 T and 20 kHz.
  • the cores consisting of the amorphous soft magnetic alloy, which are annealed and cooled under air in a longitudinal field, or without a magnetic field are completely equivalent to conventional permalloys in regard to their loss values
  • the permeability of ⁇ 4 is considerably increased by the annealing and cooling in air in relation to the unannealed core, although less so than through annealing with hydrogen.
  • the maximum permeability ⁇ max in relation to the unannealed core, during annealing and cooling under air in a longitudinal field drops slightly, and during annealing and cooling under air without a magnetic field, or in the transverse field, it decreases approximately by a factor of 5 to 10.
  • the decrease in the coercive force is less pronounced during annealing and cooling in air than during annealing and cooling in hydrogen.
  • the remanence and the remanence ratio were thereby even further decreased to approximately 30 and 45% by comparison to the cooling in the longitudinal field at a cooling velocity of 200° C. per hour, and thus an even flatter hysteresis curve was obtained in each instance.
  • the relative permeabilities ⁇ 4 and ⁇ max at a cooling velocity of 1200° C. per hours, dropped to approximately 50% and 30% respectively, and at a cooling velocity of 10° C. per hour said permeabilities dropped to approximately 6% and 7%, respectively, of the values obtained after cooling at 200° C. per hour.
  • the magnetic hysteresis losses after cooling at 1200° C. per hour increased by approximately 30 percent, and after cooling at 10° C.
  • the range of the average cooling rate of approximately 100° to 250° C. per hour is therefore particularly advantageous for the cooling-off process in the longitudinal field in air due to the relatively high permeabilities obtainable and the low magnetic (or hysteresis) losses with a simulataneously already very flat slope (or gradient) of the hysteresis curves.
  • Magnetic cores are made using the procedures of Example 1 and the product cores are subjected to a series of annealings followed by controlled coolings using the technique of Example 1 to 4. Specifically, the annealing temperature in each case was about 400° C. Referring to Table II, the first three alloys cited therein were each annealed for about one hour, and each of the remaining four was annealed for about four hours. The cooling velocity was about 200° C. per hour.

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US06/144,895 1977-02-26 1980-04-29 Reducing magnetic hysteresis losses in cores of thin tapes of soft magnetic amorphous metal alloys Expired - Lifetime US4314594A (en)

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DE2708472 1977-02-26
DE19772708472 DE2708472A1 (de) 1977-02-26 1977-02-26 Verfahren zum herabsetzen der ummagnetisierungsverluste in duennen baendern aus weichmagnetischen amorphen metallegierungen
DE2709626A DE2709626C3 (de) 1977-03-05 1977-03-05 Verfahren zum Herabsetzen der Ummagnetisierungsverluste in dünnen Bändern aus weichmagnetischen amorphen Metallegierungen
DE2709626 1977-03-05

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Cited By (17)

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US4368447A (en) * 1980-04-30 1983-01-11 Tokyo Shibaura Denki Kabushiki Kaisha Rolled core
US4487812A (en) * 1982-07-22 1984-12-11 Nippon Steel Corporation Magnetic amorphous alloy sheet having a film thereon
US4517017A (en) * 1981-02-10 1985-05-14 Tokyo Shibaura Denki Kabushiki Kaisha Temperature sensitive amorphous magnetic alloy
US4745536A (en) * 1982-12-23 1988-05-17 Tokyo Shibaura Denki Kabushiki Kaisha Reactor for circuit containing semiconductor device
US4763030A (en) * 1982-11-01 1988-08-09 The United States Of America As Represented By The Secretary Of The Navy Magnetomechanical energy conversion
US4865664A (en) * 1983-11-18 1989-09-12 Nippon Steel Corporation Amorphous alloy strips having a large thickness and method for producing the same
US5439534A (en) * 1991-03-04 1995-08-08 Mitsui Petrochemical Industries, Ltd. Method of manufacturing and applying heat treatment to a magnetic core
US6176943B1 (en) 1999-01-28 2001-01-23 The United States Of America As Represented By The Secretary Of The Navy Processing treatment of amorphous magnetostrictive wires
US20020098677A1 (en) * 2000-05-31 2002-07-25 Micron Technology, Inc. Multilevel copper interconnects with low-k dielectrics and air gaps
US6509590B1 (en) * 1998-07-20 2003-01-21 Micron Technology, Inc. Aluminum-beryllium alloys for air bridges
US20030209287A1 (en) * 1999-05-20 2003-11-13 Richard Wood Magnetic core insulation
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US20040217481A1 (en) * 2000-01-18 2004-11-04 Micron Technology, Inc. Structures and methods to enhance copper metallization
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US7262505B2 (en) 2000-01-18 2007-08-28 Micron Technology, Inc. Selective electroless-plated copper metallization
US8779596B2 (en) 2000-01-18 2014-07-15 Micron Technology, Inc. Structures and methods to enhance copper metallization
US20040217481A1 (en) * 2000-01-18 2004-11-04 Micron Technology, Inc. Structures and methods to enhance copper metallization
US20090243106A1 (en) * 2000-01-18 2009-10-01 Farrar Paul A Structures and methods to enhance copper metallization
US7402516B2 (en) 2000-01-18 2008-07-22 Micron Technology, Inc. Method for making integrated circuits
US20040206308A1 (en) * 2000-01-18 2004-10-21 Micron Technologies, Inc. Methods and apparatus for making integrated-circuit wiring from copper, silver, gold, and other metals
US20050023699A1 (en) * 2000-01-18 2005-02-03 Micron Technology, Inc. Selective electroless-plated copper metallization
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US7091611B2 (en) 2000-05-31 2006-08-15 Micron Technology, Inc. Multilevel copper interconnects with low-k dielectrics and air gaps
US20020098677A1 (en) * 2000-05-31 2002-07-25 Micron Technology, Inc. Multilevel copper interconnects with low-k dielectrics and air gaps
US20040164419A1 (en) * 2000-05-31 2004-08-26 Micron Technology, Inc. Multilevel copper interconnects with low-k dielectrics and air gaps
US7067421B2 (en) 2000-05-31 2006-06-27 Micron Technology, Inc. Multilevel copper interconnect with double passivation
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FR2382082A1 (fr) 1978-09-22
CA1099406A (en) 1981-04-14
NL176090B (nl) 1984-09-17
IT1093826B (it) 1985-07-26
NL7801282A (nl) 1978-08-29
ATA135178A (de) 1980-09-15
SE7801353L (sv) 1978-08-27
FR2382082B1 (sv) 1983-12-09
SE439399B (sv) 1985-06-10
IT7820435A0 (it) 1978-02-21
GB1548124A (en) 1979-07-04
JPS53108026A (en) 1978-09-20
NL176090C (nl) 1985-02-18
AT362154B (de) 1981-04-27
JPS5934781B2 (ja) 1984-08-24

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